Evaluation of Mechanical Properties of Sintered Hot Upset Forged Square Cross Section Bars of...

International

OPEN ACCESS Journal

Of Modern Engineering Research (IJMER)

| IJMER | ISSN: 2249–6645 | www.ijmer.com | Vol. 4 | Iss. 3 | Mar. 2014 | 62 |

Evaluation of Mechanical Properties of Sintered Hot Upset

Forged Square Cross Section Bars of Chromium-Molybdenum

Low Alloy Steels

1Hemlata Nayak,

2C. M. Agrawal,

3K. S. Pandey

1, 2PhD. Research Scholar, Ex. Professor,Department of Mechanical Engineering, MANIT, BHOPAL, M. P.,

India 3Professor, Department of Metallurgical and Materials Engineering,National Institute of Technology,

Tiruchirapalli-620015 Tamilnadu, India

I. Introduction Past seventy years have witnessed a tremendous growth in the area of powder perform forging/

extrusion/rolling either cold/warm or hot to produce components to near net shape with almost one hundred per

cent density. Further it has been believed over the past several decades that higher is the density, improved are

the mechanical properties, but, the last remaining residual porosity becomes very vital to all related properties of

the product .However, the reports also indicate that merely attaining the high density is not an index of improved mechanical properties. This very aspect can be referred elsewhere[1-3].The conventional P/M route

has been to consolidate the metal or blended powders in a suitable die, punch and bottom insert assembly at

enhanced pressures and sintering them under the protective or the reducing atmospheres for a given length of

time and same were employed directly in service. However, the demands raised by the automobile, nuclear and

space industries were that the parts produced must serve the requirements of structural applications and, hence,

one of the deformation processes were thought to be essential to be employed even though an open option of

liquid phase sintering or liquid phase infiltration processes were available to enhance sound metallurgical bonds.

But, the period beyond seventies saw a sea change in producing forged P/M parts for direct applications with

improved efficiency. In majority of the cases, P/M forged parts exhibited higher range of mechanical properties

which were isotropic in nature then the conventionally produced ingot metallurgy (I/M) parts.

Abstract: Present investigation pertains to evaluate the tensile properties of sintered hot forged and oil quenched and also homogenized, but furnace cooled specimens which were machined from

square cross section bars of approximate dimensions of ~13mm x ~13mm x~100±5mm of Fe-

0.16%C, Fe-0.16%C-0.7%Mn, Fe-0.16%C-1.0%Cr-0.55%Mo and Fe-0.16%C-2.25Cr-1.05%Mo

P/M steels prepared from elemental powders. Green compacts of homogeneously blended powders

of all compositions were prepared with initial aspects ratio of 1.34 with diameter being 27.5mm

using suitable compaction die set assembly on 1.0MN capacity UTM to a density level of 0.85±0.01

of theoretical employing controlled pressures in the range of 490±10MPa and taking pre – weighed

powder blends. All green compacts were protected during sintering by applying thin film of

indigenously developed ceramic coating on the entire surfaces. Ceramic coated compacts were

sintered in an electric muffle furnace at 1373±10K for a period of 120 minutes. All sintered

preforms of each com position were hot forged on a 1.0MN capacity friction screw press to square cross section bars of afore mentioned dimensions. Once the forging operation was completed 10-12

bars were quenched in linseed oil and nearly 12 bars were homogenized at sintering temperature

for one hour and then cooled inside the furnace itself. Standard tensile specimens were machined

and tested on Hounsfield Tensometer for evaluating tensile properties which were appreciably close

to the properties reported in literature for the above steels. Microstructure of specimens containing

chromium and molybdenum exhibited few un-dissolved particles along with the presence of fine

pores. SEM Fractography revealed mixed mode failure mostly ductile and partly brittle. These

steels also exhibited adequate ductility as is exhibited by conventionally produced steels. Thus, this

investigation shows the way how to produce high density P/M steels which can be used in structural

applications.

Key Words: applications, bars, composition, density, dissolved, ductility, failure, furnace cooled,

fractography, hot forged, microstructures, sintered, structural, tensile.

Evaluation of Mechanical Properties of Sintered Hot Upset Forged Square Cross Section Bars of....


P/M parts are practically well suited for fast high volume production of countless parts in the

automotive, various appliances, agricultural equipment, business machines, electrical and electronic, power

tools ordnance and machine tools industries. However, they also find extensive applications in the aerospace,

nuclear and other industries [4]. Thus, powder metallurgy offers the engineers and scientists, a means of

conserving materials, minimizing machining and by securing a uniform product at reasonable costs [5]. In

industries, the forming of structural components from porous materials, either directly from atomized powders

or from blended powders, but, sintered preforms is becoming a popular route. This is due to the fact that P/M forming processes result in savings in energy and materials in addition to quality improvement. In automotive

industries, the weight reduction results in favourable operating conditions of the engine in terms of reduced

exhaust gas emissions and vibrations. Thus, lowering down the fuel consumptions .Connecting rod is the bulk

component, i.e., required in automobiles, and, hence, the P/M forming route is in strong competition with the

conventional processes such as casting and forgings routes [6].

In powder preform forging or hot isostatic pressing, the density and the mechanical properties of

components and parts is raised to values to those of wrought products [7]. Plastic deformation of sintered

powder materials are similar to that of conventionally fully dense materials, but, there are additional

complications due to the substantial volume fraction of voids in the perform materials. In particular, the voids

must be eliminated during deforming operation so that a sound metallurgical structure is obtained [8]. The

forging of sintered powder performs has been shown to be a process capable of producing higher density P/M parts for high stress applications where porosity must be minimized or completely eliminated. Mechanical

properties of powder forged parts depend upon the processing parameters, the composition, the sintering time

and forging operations [9]. Pores present in a P/M parts act as stress raisers and also provide initiation sites for

corrosion, especially in an environment containing chloride ions. However, industrial use of stainless P/M

products has increased in the recent years due to their improved corrosion properties and at relatively low cost.

Porosity in P/M parts makes them highly susceptible to crevice corrosion [10]. However, the probability of

fracture is mainly dependent upon the volume fraction of pores and only to a small extent depends on pore size

[11]. However, the fatigue properties in P/M parts can be referred elsewhere [12-16]. But, the fatigue strength of

hot forged and shot pinned P/M parts are detailed elsewhere [17, 18] and other stressed P/M parts can be further

referred in literature [19-23]. Apart from these, the mechanical properties of differently produced ferrous based

P/M steels of challenging in nature can be referred elsewhere [24-29].

Systems selected to be produced through elemental powders were (A) Fe-0.16%C, (B) Fe-0.16%C-0.70%Mn, (C) Fe-0.16%C-1.0%Cr-0.55%Mo, and (D) Fe-0.16%C-2.25%Cr-1.05%Mo steels. Applications of

(A) category of steels i.e., Fe-0.16%C steels are that they are used for rivets, wires, nails, chains, stampings,

seam welded pipes, hot and cold rolled strips, sheets and plates for general purposes, ship plates, boiler plates,

cams and shafts, stay bolts, wheel hubs, brake housings and brake pedal levers. Since, B grades of steels, i.e.,

Fe-0.16%C-0.7%Mn steels contain 0.7%Mn which neutralizes the harmful effects of sulphur by forming MnS

which melts at higher temperatures. Further manganese enhances the tensile strengths, imparts freedom from

blow holes, deoxidizes the steel and produces fine grained steel and improves surface quality. Manganese can be

used as structural materials as well. However, (C) grade of steels, i. e., Fe-0.16%C-1.0%Cr-0.55%Mo, and (D)

grade of steels, i. e., Fe-0.16%C-2.25%Cr-1.05%Mo containing chromium and molybdenum as alloying

elements which are known to induce beneficial effects to these steels. Chromium is added in steels as it is

comparatively less expensive and imparts many useful characteristics to the steel. Readily combines with carbon in preference to iron. Cr offers resistance to oxidation. However, the addition of molybdenum in steels refines

grains, enhances harden ability and improves high temperature properties. Thus, Cr-Mo steels possess good

mechanical properties and sufficiently adequate machinability as molybdenum enhances the beneficial effects of

chromium in chromium molybdenum steels and find applications as low alloy structural steels. These steels

have good resistance to corrosion and oxidation and offer high creep resistance. Therefore, the above four steels

have been selected for the present investigation. Basically, Cr and Mo are strong carbide formers. Cr raises

tensile strengths, hardness, wears resistance and hardenability and makes the steel stainless when added beyond

12%. These steels find applications in general purpose structural applications such as ball bearing steels, spring

steels, hard magnetic steels, and, stainless steels. Since, molybdenum is a strong carbide former, imparts high

temperature strengths, enhances resistance to creep, minimizes temper embrittlement, and increases the

resistance to corrosion of high chromium steels, and, therefore, molybdenum assists in case hardening steels, Hot work steels, High speed steels, and, Non magnetic steels.

Aim of the present investigation is to produce and evaluate the tensile properties of hot forged square

cross section (~13mm x ~13mm) bars with an approximate lengths of 100±05mm of Fe-0.16%C, Fe-0.16%C-

0.7%Mn, Fe-0.16%C-1.0%Cr-0.55%Mo,and, Fe-0.16%C-2.25%Cr 1.05%Mo steels prepared from elemental

powders which were suitably mixed, homogeneously blended, compacted, sintered, hot forged to square cross-

section bare and heat treated differently. Mechanical properties are suitably related to microstructure and SEM

fractographs.



II. Experimental Details 2.1 Materials Required

Atomized iron powder of -180 um was procured from M/s. Sundaram Fasteners Pvt. Limited,

Hyderabad, and Andhra Pradesh, India. Manganese, chromium and molybdenum powders of -37 um were obtained from M/s. The Ghrishma Speciality Powders Limited, Mumbai, Maharashtra, India. However, the

graphite powder of less than 5 micron was supplied by the M/s. Ashbury Graphite Inc., New Jersey, U.S.A.

2.2 Tooling and Equipment

High-Carbon High-Chromium die steel was required to fabricate the mother die, punch, and the bottom

insert for compaction of powder blends. Molybdenum-di-sulphide paste was needed to be used during

compaction as a die wall lubricant. In house designed, fabricated die, punch and bottom insert were suitably heat

treated and tempered. However, hot forging die set was fabricated from molybdenum hot die steel. These were

suitably heat treated and tempered.

2.3 Powder and Powder Blend Characteristics

Basically, the ability of a metal powder blends to be effectively compacted and the resulting properties of the compacts before and after sintering are influenced to a substantial degree by the characteristics of the

starting powdered material. The basic powder characteristics required to be assessed include, sieve size analysis,

apparent density, flow rate and compressibility. Sieve size analysis of basic iron powder is given in Table 1,

and, Table 2 shows the flow rates, apparent densities and the compressibility for iron powder and other powder

blends to yield the final composition of Fe-0.16%C, Fe-0.16%C-0.7%Mn, Fe-0.16%C-1.0%Cr-0.55%Mo, Fe-

0.16%C-2.25%Cr-1.05%Mo steels after sintering. Manganese, chromium and molybdenum powders taken in

the present investigation were of -37 microns.

Table 1 Sieve Size Analysis of Iron Powder

Sieve size, µm Powder Size Distributio

Wt %

retained

-180

+ 150

-150

+125

-125

+106

-106

+90

-90

+75

-75

+63

-63

+53

-53

+37 -37

Wt% powder

retained 1.52 1.83 23.12 1.11 21.86 2.21 18.60 13.62 16.11

Cum, Wt%

powder Ret. 1.52 3.35 26.47 27.58 49.44 51.65 70.25 83.87 99.98

2.4 Powder Blend Preparation

Powder mixes of Fe-0.16%C, Fe-0.16%C-0.7%Mn, Fe-0.16%C-1.0%Cr-0.55%Mo and Fe-0.16%C-

2.25%Cr-1.05%Mo were separately kept in a standard stainless steel pots with a powder mix to porcelain balls

of 10 - 15mm diameter in the weight ratio of 1.1:1. Pot lids were securely tightened, and, the pots were fixed on

the pot mill and the mill was switched on. The blending operation was carried out for a period of 32 hours which

yielded homogeneous powder blends. Homogeneity of powder blends were ascertained by taking nearly 120±10

g of each of the powder mixes from each pot and were used for measuring the flow rates, and apparent densities.

Immediately, after the completion of measurements of flow rates and apparent densities, the powder mixes were

returned back to their respective pots, and, the pot lids were tightened once again and were placed back on the potmill and securely fixed and then the mill was switched on again, This operation was repeatedly carried out

till the last thee consecutive readings of flow rates and apparent densities were almost constant independently.

This ensured the homogeneity of the powder blends. Thus, the time of blending was experimentally found to be

32 hours and the same was fixed.

Table 2 Basic Properties of Iron, Fe-0.16%C, Fe-0.16%C-0.7%Mn, Fe-0.16%C-1.0%Cr-0.55%Mo and Fe-

0.16%C-2.25%Cr-1.05%Mo Powder Blends.

Sl.

No. Systems

Apparent

density, g/cc

Flow rate by Hall

Flow Meter, S/100g. Remarks

1 Iron 2.973 51.52 6.594g/cc at 400±10MPa

2 Fe-0.16%C 2.934 48.67 6.751g/cc at 450±10MPa

3 Fe-0.16%C-0.7%Mn 2.990 50.93 6.756g/cc at 375±10MPa

4 Fe-0.16%C- 1.0%Cr-0.55%Mo 3.010 47.01 6.74g/cc at 450±10MPa

5 Fe-0.16%C-2.25Cr -1.05%Mo 3.090 46.77 6.732g/cc at 375±10MPa



2.5 Compact Preparation from Iron powder and the Powder Blends

Green compacts of iron powder and the above prepared powder blends were prepared on a 1.0 MN

capacity Universal Testing Machine. Compacts of initial aspect ratios of 1.34 with the diameter being 27.75mm

were prepared by applying pressures in the range of 540±10 M Pa in the relative density range of 0.85±0.01of

theoretical by taking accurately pre-weighed iron powder and powder blends respectively. In all, twenty four

compacts of each composition were prepared. A schematic diagram shown in fig.1 depicts the compaction

assembly for the compaction of iron powder and powder blends.

Figure 1 Complete Compaction Assembly - Schematic Diagram

2.6 Application of Indigenously Developed Ceramic Coating and Drying

Entire surfaces of all compacts of all compositions were coated with a thin film of indigenously

developed ceramic coating [30] and the same was allowed to dry for a period of 12 hours under an ambient

conditions. A second coat of the same coating was now applied on the entire surfaces of all the compacts once

again, but, this time 900 to the previous coating. This second coating was also allowed to dry under the

aforementioned conditions for a further period of 12 hours.

2.7 Sintering and Hot Forging To Square Cross-Section Bars

The ceramic coated compacts of all compositions were separately sintered in an electric muffle furnace in

the temperature range of 1373±10K for a period of 120 minutes. The sintered compacts of H/D ratio of 1.34 with a diameter of 27.75mm were hot forged to square cross-section (13mmx~13mm) bars of approximate

lengths of 100±5mm. Twelve forged bars of each compositions were kept inside the furnace chamber and

homogenized for a period of sixty minutes at the sintering temperature itself, and, subsequently cooled to room

temperature inside the furnace chamber by switching off the furnace. Apart from the above, other sets of twelve

sintered compacts of each composition were also forged to similar types of bars and then quenched in linseed oil

kept at room temperature separately.

III. Results and Discussions

3.1 Dimensional Measurements and Tensile Properties

Standard tensile specimens as per specifications given elsewhere [27] were machined from the Fe-

0.16%C, Fe-0.16%C-0.7%Mn, Fe-0.16%C-1.0%Cr-0.55%Mo and Fe-0.16%C-2,25%Cr-1.05%Mo sintered

powder metallurgy steels hot forged to square cross-section bars under two different conditons of heat

treatments, namely, sintered hot forged and oil quenched (SFOQ) and sintered hot forged, but, homogenized at

1373±10K for sixty minutes and furnace cooled (SFHFC). Prior to conducting the tensile tests, the dimensional

measurements such as initial gauge length (L0), initial diameter (D0) within the guage length were under taken and recorded. During and after fracture, the final gauge length (Lf) and final diameter (Df) at the point of

fracture were also measured and recorded. Further peak load (Ppl, Kg) qand fracture load (Ffl, Kg) were also

recrded during and after carrying out the tensile tests respectively. All tension test experiments were carried out

on a 0.02 MN capacity bench type Haunsfield Tensometer. Original area of cross-section (A0, mm2) for all

specimens were calculated and all experimental and measured parameters are provided in Table 3. Perusal of

this table very clearle reflects that the area of cross-section at the fracture point has decreased irrespective of the

heat treatments meted out to the specimens and their compositions. Further the area of reduction in tension

tested specimens were observed to be more when the



Table 3 Initial and Final Dimensions of the Tensile Specimens of Four Different Sintered Hot

Forged P/M Steels to Square -Cross Section Bars

Steel Composition Treatment

Dimensional measurement Peak

Load

Area of Cross

section

Fracture

Load

L0

mm

D0

mm

Lf

mm

Df

mm Ppl, Kg A0 Af

Ffl

Kg

Fe-0.16%C SFOQ 5.17 3.74 6.67 3.18 761 10.96 7.94 724

SFHFC 5.18 3.85 7.66 2.68 428 11.62 5.64 357

Fe-0.16%C-0.55%Mo SFOQ 5.59 3.74 7.01 3.42 810 10.98 9.20 728

SFHFC 5.73 3.76 7.76 3.00 486 11.08 7.08 342

Fe-0.16%C-1%Cr-

0.55%Mo

SFOQ 6.07 3.75 6.5 2.54 769 11.04 9.85 738

SFHFC 5.43 3.71 7.72 3.26 307 10.80 8.34 269

Fe-0.16%C-2.25%Cr-

1.05%Mo

SFOQ 6.54 3.76 7.52 3.68 744 11.10 10.21 738

SFHFC 7.19 3.72 8.56 3.34 394 10.88 8.69 375

Specimens were subjected to homogenization step followed by furnace cooling. Apart from this, these

specimens exhibited increased elongations compared to the specimens which were forged and directly quenched

in oil. In order to justify the above, the Table 4 has been constructed based on the experimental data and

standard calculations of tensile properties such as tensile strengths, fracture (true and engineering) strengths, per

cent age elongation and per cent area reduction including true tensile and true area strains at fracture. Further,

this table shows the hardness taken on each of the specimens under all conditions of heat treatments. Directly

forged and oil quenched specimens have shown higher values of tensile strengths compared to the specimens which were forged, homogenized and furnace cooled. Apart from these, it is also observed that the forged-

homogenized and furnace cooled specimens have demonstrated quite high values of ductility compared to the

forged and oil specimens. An introduction of homogenization step for an hour at the sintering temperature

followed by furnace cooling has resulted in a substantial drop in tensile strength with an enhancement in

ductility, i.e., toughness. Similarly, the hardness values have also dropped correspondingly on homogenization.

Table 4 Calculated Tensile Properties of Four Different Hot Forged Low Alloy P/M Steel Bars

Steel

Compositio

n

Heat

Treatments

Tensile Properties

T.S.

F.S. , MPa

%El.

Strain at

Fract. %

A.R.

Area

Strain

ln(A0/Af)

Har

dnes

s

Engg True Engg True

Fe-0.16%C SFOQ 694.3 661 912 28.99 0.29 0.276 27.58 0.323 249

SFHFC 368.5 307 633 47.69 0.477 0.515 51.46 0.723 161

Fe-0.16%C

0.7%Mn

SFOQ 738 663 792 25.34 0.253 0.162 16.23 0.177 256

SFHFC 438.7 309 483 35.43 0.354 0.361 36.10 0.448 169

Fe-0.16%C-

1%Cr-

0.55%Mo

SFOQ 697 669 749 7.03 0.070 0.108 10.76 0.0680 269

SFHFC 284 248 323 42.17 0.422 0.228 22.79 0.259 157

Fe-0.16%C-

2.25 %Cr-

1.05%Mo

SFOQ 670 665 723 14.93 0.149 0.080 7.95 0.083 287

SFHFC 362 345 431 23.22 0.232 0.201 20.11 0.224 251

3.2 Microstructural Details Figs. 2, 3, 4, 5, 6, 7 and 8 are shown as the metallographs exhibiting the microstructural details of Fe-

0.16%C, Fe-0.16%C-0.7%Mn, Fe-0 .16%C-1.0%Cr-0.55%Mo, and Fe-0.16%C-2.25%Cr-1.05%Mo steels

processed using elemental powders which were homogeneously blended, compacted, suitably coated with the

indigenously developed ceramic coating to protect them during sintering were sintered, and, then hot forged to

square cross-section bars. Equal numbers of these bars were oil quenched and homogenized for a period of one

hour at the sintering temperature itself and then furnace cooled. Microstructures have well corresponded to the

tensile properties that are revealed from the tensile test results. Fig. 2 shows the microstructures which are

mostly ferrite with few fine pores uniformly distributed. These microstructures correspond to as forged, homogenized and furnace cooled condition. Whereas, the fig. 3, represents the structure of the same steel under

the condition of sintered, forged and oil quenched condition. Similarly figs. 3(a), (b) and (c) are shown from

three different locations of the hot forged, but, homogenized and furnace cooled condition showing mostly



ferrite and few scattered but rounded pores well within the structure itself. However, fig. 4 represents the same

steel under the as forged and oil quenched condition. Similarly figs. 5 and 6 correspond to Fe-0.16%C-1.0%Cr-

0.55%Mo steel under two above mentioned conditions. Likewise figs. 7(a), 7(b) and 7(c) and fig.8 correspond to

the P/M steel of composition Fe-0.16%C-2.25%Cr-1.05%Mo under the above conditions, i.e., under the forged,

homogenized and the furnace cooled condition. and also under the forged and oil quenched condition. The

general observations of these micro-structures reveal that the homogenization step has introduced grain growth

and structural modification. These structures clearly show that they are under the completely stress relieved condition. These structures very closely corresponded to the tensile properties as well as the respective hardness

values. Further observation reveals that the microstructure of forged and homogenized specimens contain

rounded and evenly distributed pores, but, they are very few in numbers whereas, the microstructure

corresponding to forged and oil quenched conditions did exhibit the presence of rounded pores but unevenly

distributed in the microstructure. Apart from these, the steels containing chromium and molybdenum have

shown carbide formation and also at few places un-dissolved chromium and molybdenum particulate structures

are evidently seen. Such particulate structures are seen in both types of heat treated specimens.

(a) SFHFC CONDITION(2% Nital) Mag. 250X (b)SFOQ CONDITION (2% Nital) Mag. 250X

Figure 2 Microstructures of Sintered Forged Fe-0.16%C Steel Under Two different Heat Treated

Condition (etchant; 2% Nital)

(a) Centre(100X)

(b ) Middle of centre and edge(100X) (c) Edge(100X)

Figure 3 Microstructures shown at Three Different Locations of the Cross-section Bars of

Fe-0.16%C-0.7%Mn P/M Steel SFHFC Condition (etchant; 2% Nital)

Figure 4 Microstructures shown at the Centre Locations of the Cross-section Bar of Fe-0.16%C-0.7%Mn

P/M Steel SFOQ Condition at 250X; (etchant; 2% Nital).



(a) Centre(250 X) (b) Edge(250 X)

Figure 5 Microstructures shown at the Centre and at the Edge Locations of the Cross-section Bar of Fe-

0.16%C-1.0%Cr-0.55%Mo P/M Steel SFHFC Condition (etchant; 2% Nital)

Magnification = 100X

Figure 6 Microstructures shown at the Centre Locations of the Cross-section Bar of Fe-0.16%C-1.0%Cr-

0.55%Mo P/M Steel SFOQ Condition (etchant; 2% Nital).

(a) Centre(100 X) (b) Edge(100 X)

Figure 7 Microstructures shown at the Centre d at the Edge Locations of the Cross-section Bar of Fe-

0.16%C-2,25%Cr-1.05%Mo P/M Steel SFHFC Condition (etchant; 2% Nital)

(a) Centre(400X) (b) Middle of centre and edge(400X) (c) Edge(400X)

Figure 8 Microstructures shown at the Three DifferentLocations of the Cross-section Bar of Fe-0.16%C-

2.25%Cr-1.05%Mo P/M Steel Under SFOQ Condition (etchant; 2% Nital).



3.3 SEM Fractography Fractured Surfaces of Tensile Tested Specimens all four Steels Investigated Fractographs shown through figs. 9 to 12 reveal the exact nature of the fractured surfaces of the tensile

tested specimens under various conditions. Fig. 9 (a) shows the fractographs corresponding to Fe-0.16%C P/M

steel which has been homogenized and furnace cooled. This structure clearly shows large number of dimples

indicating the failure mode to be highly ductile and the same is very well supported by the tensile properties that

are fairly high, which is an index of high ductility (~48%elongation and ~52% area reduction). Similarly the

fractographs represented through fig. 9 (b) also depicts fairly large number of dimples and at places fine, but, rounded porosities in good numbers are also visible. Fractured pieces of this specimen when visually examined

have exhibited cup and cone type separation of the two corresponding counter parts. High level of ductility

(29% elongation and 28% area reduction) is recorded. Similarly the steel corresponding to Fe-0.16%C-0.7%Mn

composition exhibited quite ductile mode of failures under both the conditions of heat treatments.However,

under the homogenized and furnace cooled condition the failure has advanced through the coalescence of

residual pores, but, the failure remained ductile only (fig.10(a). Once again the similar situation existed when

the steel has been forged and oil quenched. Even though, the steel exhibited high strength values, the ductility

remained fairly high indicating that the steel under this condition also remained fairly tough and thus the failure

remained quite ductile as is evident through the fig.10(b).

(a) SFHFC (b) SFOQ Figure 9 SEM Fractographs of Tensile Tested Specimen fractured Surfaces of Fe-0.16%C P/M Steel

Figs. 11 and 12 showing the SEM fractographs corresponding to the steel composition of Fe-0.16%C-1.0%Cr-

0.55%Mo. This steel SEM fractographs under the forged, homogenized and furnace cooled condition shows

large number of dimples an index of ductile mode of failure (fig. 11(a)) which is ably supported by the tensile

test results exhibiting high percentage of elongation (~42%) and per cent area reduction (~23%).SEM

fractographs shown in fig. 11(b) corresponds to the same steel, but, under sintered, forged and oil quenched

condition. Even though dimples

(a)

SFHFC (b)SFOQ

Figure 10 SEM Fractographs of Tensile Tested Specimen fractured Surfaces of Fe-0.16%C-0.7%Mn P/M

Steel Under Two conditions of Heat Treatments.



(a) SFHFC (b) SFOQ

Figure 11 SEM Fractographs of Tensile Tested Specimen fractured Surfaces of Fe-0.16%C-1.0%Cr-

0.55%Mo P/M Steel Under Two conditions of Heat Treatments.

(a) SFHFC

(b) SFOQ

Figure 12 SEM Fractographs of Tensile Tested Specimen fractured Surfaces of Fe-0.16%C-2.25%Cr-

1.05%Mo P/M Steel Under Two conditions of Heat Treatments.

IV. Conclusions Based on the experimental data on tensile properties of four different low alloy steels produced through powder metallurgical routes using elemental powders via homogeneous blending, compacting, sintering and hot

forging to square cross-section bars and heat treating them under two distinct conditions such as sintering,

forging and oil quenching (SFOQ) and sintering, forging and homogenizing at the sintering temperature for a

period of an hour followed by cooling them inside the furnace itself and after analyzing the data critically, the

following main conclusions have emerged:

1. Four P/M steels investigated in the present investigation produced from the elemental powders which were

sintered, forged and oil quenched have shown improved strengths, but, reduced ductility compared to the

steels which were sintered, forged, homogenized and furnace cooled which have shown high degree of

ductility,

2. Microstructures of all the four steels have clearly shown the presence of porosities which were mostly

rounded in the event of homogenized for a period of one hour at the sintering temperature and cooling inside the furnace itself. However, at places in the microstructures corresponding to steels containing chromium

and molybdenum, few un-dissolved particles of these elements are also present,

3. Tensile tested specimens fractured in a cup and cone type in all the steels except for the steel Fe-0.16%C

which was highly cup and cone type when they were homogenized and furnace cooled. However, the forged

and oil quenched specimens have exhibited mixed mode of failures,



4. SEM fractographs corresponding to steels which were produced by sintering, forging, homogenizing

and furnace cooling have exhibited mostly ductile failures as it contained large number of dimples which are an

index of ductile failures, but, the quenched steels in their corresponding fractographs have shown fairly good

amount of dimples as well as presence of particle de-lamination which is an index of mixed mode of failures,

Finally summarizing the outcome of the present investigation, it is, established that there exists a

certainty of producing the quality P/M products by using elemental powders and their homogeneously blended

mixes to required compositions of the given steel/s. The higher mechanical properties such as strength and sound metallurgical structures along with the enhanced toughness under the sintered forged and oil quenched

condition. However, under sintered, forged, homogenized and furnace cooled condition, the strength and

toughness attained are suitable for producing quality structural parts. Thus, the present investigation opens up a

new area of research to produce structural components using elemental powders.

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Evaluation of Mechanical Properties of Sintered Hot Upset Forged Square Cross Section Bars of...

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